Effects of Microstructure Evolution on Fretting Wear Behaviors of 25CrNi2MoVE Steel under Different Tempering States
Abstract
:1. Introduction
2. Experimental Details
2.1. Material and Heat Treatment
2.2. Material Characterization
2.3. Fretting Wear Test and Calculation of Volumetric Wear Rate
2.4. Measurements of Worn Surface Roughness (WSR)
3. Results and Analysis
3.1. Fretting Wear Behaviors
3.1.1. Coefficient of Friction
3.1.2. Worn Morphologies and Volumetric Wear Rate (Kv)
3.1.3. Worn Surface Roughness Rz
3.2. Relationship between Microhardness and Wear Properties
3.3. Relationship between Microstructure Evolution and Wear
3.3.1. Initial Microstructure under As-Received State (AR)
3.3.2. Tempered Microstructure after Normalizing (N850, NT200, NT350, NT550, NT850)
3.3.3. Tempered Microstructure after Quenching (NQ850, NQT200, NQT350, NQT550, NQT850)
3.4. Wear Mechanisms
4. Conclusions
- In AR state (spheroidization annealing), coarse ferrite grain, pearlite grain and carbide precipitates are the main reasons for the low wear resistance.
- Normalizing significantly reduced the grain and carbide precipitate size of the original material and obtained the beneficial M5C2 phase and a low worn surface roughness. Tempering at 200 °C can promote the formation and refinement of bainite, and the presence of metastable M6C, M3C and M5C2 carbides can also improve wear performances. From 350 °C to 850 °C, bainite gradually reduced or dissolved, grain boundary disappeared and volumetric wear rate, coefficient of friction and worn surface roughness increased.
- Martensite multi-phase structure and M2C and M5C2 carbides can be generated by quenching to improve wear resistance and worn surface roughness. After tempering at 200 °C, the tempered martensite structure was obtained, which effectively alleviated the fatigue wear problems. When tempering at 350 °C, the tempered troostite increased the degree of adhesive wear and worn surface roughness, but the good continuity of surface oxide film provides good wear resistance. The excessive tempering temperature resulted in the decrease of material strength and deterioration of volumetric wear rate.
- In AR state, the coarse grain caused an easy slip tendency, leading to a high adhesive wear and fatigue wear degree. After normalizing, the grains are refined, and the fatigue wear is improved accordingly. As the tempering temperature increased, the hardness and work hardening tendency decreased and the degree of abrasive wear gradually decreased. For quenched samples, the staggered lath martensite structure greatly enhanced the hardness, and adhesive wear and fatigue wear became the main mechanisms. As the tempering temperature increased, fatigue wear improved. Abrasive wear tends to increase first and then decrease, and adhesive wear gradually becomes the main wear mechanism.
Author Contributions
Funding
Acknowledgments
Conflicts of Interest
Nomenclature
Ac1 | start temperature of pearlite to austenite transformation during heating [°C] | Ac3 | finish temperature of ferrite to austenite transformation during heating [°C] |
Ms | martensite start temperature during cooling [°C] | Mf | martensite finish temperature during cooling [°C] |
V | volumetric wear loss [mm3] | h | maximum depth of the fretting wear scar on lower sample [mm] |
ρ | approximate curvature radius of the wear scar concave surface | l | maximum length of the wear scar along the fretting direction [mm] |
d | maximum width of the wear scar perpendicular to the fretting direction [mm] | Kv | volumetric wear rate [mm3/Nm] |
FN | imposed normal contact force [N] | s | relative slip distance [m] |
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Ni | Cr | Mn | Mo | C | Si | V | Al | Cu | N | P | O | S | Fe |
---|---|---|---|---|---|---|---|---|---|---|---|---|---|
2.1 | 1.55 | 0.66 | 0.3 | 0.26 | 0.26 | 0.105 | 0.097 | 0.03 | 0.0222 | 0.0135 | 0.0023 | 0.007 | Balance |
Material States | Heat Treatments | |
---|---|---|
As -received (AR) | Austenized at no less than 1120 °C, annealed at no less than 850 °C (as per manufacturer) | |
No tempering | N850 | AR + Normalized at 850 °C for30 min, air cooling |
NQ850 | N850 + Quenched at 850 °C for 30 min, oil cooling | |
Low-temperature tempering | NT200 | N850 + Tempered at 200 °C for 90 min, air cooling |
NQT200 | NQ850 + Tempered at 200 °C for 90 min, air cooling | |
Medium-temperature tempering | NT350 | N850 + Tempered at 350 °C for 90 min, air cooling |
NQT350 | NQ850 + Tempered at 350 °C for 90 min, air cooling | |
High-temperature tempering | NT550 | N850 + Tempered at 550 °C for 90 min, air cooling |
NQT550 | NQ850 + Tempered at 550 °C for 90 min, air cooling | |
Excessive temperature | NT850 | N850 + Tempered at 850 °C for 90 min, air cooling |
NQT850 | NQ850 + Tempered at 850 °C for 90 min, air cooling |
Parameters | Set Values |
---|---|
Stroke (μm) | 200 |
Frequency (Hz) | 20 |
Preloading force (N) | 5 |
Preloading time (min) | 5 |
Normal force (N) | 45 |
Loading time (min) | 30 |
Total number of wear cycles | 42,000 |
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Hu, X.; Lai, F.; Qu, S.; Zhang, Y.; Liu, H.; Wu, Z. Effects of Microstructure Evolution on Fretting Wear Behaviors of 25CrNi2MoVE Steel under Different Tempering States. Metals 2020, 10, 351. https://doi.org/10.3390/met10030351
Hu X, Lai F, Qu S, Zhang Y, Liu H, Wu Z. Effects of Microstructure Evolution on Fretting Wear Behaviors of 25CrNi2MoVE Steel under Different Tempering States. Metals. 2020; 10(3):351. https://doi.org/10.3390/met10030351
Chicago/Turabian StyleHu, Xiongfeng, Fuqiang Lai, Shengguan Qu, Yalong Zhang, Haipeng Liu, and Zhibing Wu. 2020. "Effects of Microstructure Evolution on Fretting Wear Behaviors of 25CrNi2MoVE Steel under Different Tempering States" Metals 10, no. 3: 351. https://doi.org/10.3390/met10030351